Lithium Silicate- Low Quartz Glass Ceramic

ABSTRACT

Lithium silicate-low quartz glass ceramics are described which are characterized by a combination of very good mechanical and optical properties and can therefore be used in particular as restoration material in dentistry.

The invention relates to lithium silicate-low quartz-glass ceramic whichis suitable in particular for use in dentistry, preferably for thepreparation of dental restorations, as well as to precursors for thepreparation of this glass ceramic.

Lithium silicate glass ceramics are characterized as a rule by very goodmechanical properties, which is why they have been used for some time inthe dental field, and there primarily for the preparation of dentalcrowns and small dental bridges.

U.S. Pat. No. 5,507,981 and U.S. Pat. No. 5,702,514 describe lithiumdisilicate glass ceramics which are processed to form dentalrestorations by pressing in the viscous state. However, the use of adeformable crucible is essential, which makes the processing veryexpensive.

EP 827 941 and EP 916 625 disclose lithium disilicate glass ceramicswhich can be given the shape of the desired dental restoration bypressing or machining.

EP 1 505 041 and EP 1 688 398 describe processes for the preparation ofdental restorations from lithium disilicate glass ceramics. As anintermediate product a glass ceramic with lithium metasilicate as maincrystal phase, which can be very easily machined e.g. by means ofCAD/CAM processes, is produced first. This intermediate product is thensubjected to a further heat treatment in order to form the desiredhigh-strength lithium disilicate glass ceramic. The heat treatments usedduring the process are to be chosen such that the formation of undesiredcrystal phases, such as for example cristobalite, is prevented.

WO 2013/053864 discloses lithium silicate glass ceramics which containdivalent metal oxide and can be processed to form dental restorations byhot pressing as well as by machining.

Glass ceramics are known from WO 2013/164256 which have lithiumdisilicate as main crystal phase and apatite as a further crystal phase.The glass ceramics are characterized by high chemical stability and canbe shaped to form the desired dental restorations by machining or hotpressing.

US 2015/0104655 describes glass ceramics which, depending on thecomposition and the temperature treatment chosen for thecrystallization, can contain lithium disilicate, lithium metasilicate,lithium phosphate, cristobalite, tridymite, quartz or spodumene ascrystal phases. The glass ceramics are intended in particular to veneerzirconium oxide ceramics.

However, the machining of the conventional lithium disilicate glassceramics is possible only with difficulty because of their high strengthand it therefore as a rule involves a high wear of the tools used. Thelikewise possible machining of corresponding lithium metasilicate glassceramics as precursors is much easier. However, this requires yet afurther heat treatment to produce the restoration from high-strengthlithium disilicate glass ceramic after the shaping by machining.

There is therefore a need for lithium silicate glass ceramics which areeasily machinable and do not require a further heat treatment after thisprocessing in order to give the produced dental restoration the desiredmechanical properties. The lithium silicate glass ceramics are to havenot only very good mechanical properties, but likewise also very goodoptical properties, in order that they also fulfil the high aestheticdemands which are made on a restorative dental material.

This object is achieved by the lithium silicate-low quartz glass ceramicaccording to claims 1 to 14 and 17. Also a subject of the invention arethe starting glass according to claims 15, 16 and 17, the processaccording to claims 18, 19 and 22 as well as the use according to claims20 and 21.

The lithium silicate-low quartz glass ceramic according to the inventionis characterized in that it comprises lithium silicate as main crystalphase and low quartz as further crystal phase.

It has surprisingly been shown that the glass ceramic according to theinvention unites a combination of very desirable mechanical and opticalproperties, such as are necessary precisely for a restorative dentalmaterial. The glass ceramic has a high strength and nevertheless it canbe given the shape of a dental restoration easily by machining. There isno need for a subsequent heat treatment to achieve a satisfactorystrength. It was furthermore not to be expected that very good opticalproperties can nevertheless be achieved by the provision of low quartzas further crystal phase in addition to lithium silicate as main crystalphase. This is because many additional crystal phases have a negativeeffect on the optical properties of lithium silicate glass ceramics. Forexample they can decrease the translucence and they can likewise impairthe ability of the glass ceramic to be dyed, which can lead tosubstantial difficulties in the imitation of the colour of the naturaltooth material to be replaced.

The lithium silicate-low quartz glass ceramic according to the inventionin particular comprises 59.0 to 79.0, preferably 64.0 to 78.0 andparticularly preferably 64.0 to 76.0 wt.-% SiO₂.

In another embodiment, the lithium silicate-low quartz glass ceramicaccording to the invention in particular comprises 68.0 to 79.0,preferably 69.0 to 78.0 and particularly preferably 70.0 to 76.0 wt.-%SiO₂.

It is further preferred that the lithium silicate-low quartz glassceramic according to the invention comprises 8.0 to 15.0, particularlypreferably 9.0 to 14.0 and quite particularly preferably 10.0 to 13.5wt.-% Li₂O. It is assumed that Li₂O lowers the viscosity of the glassmatrix and thus promotes the crystallization of the desired phases.

In a further preferred embodiment, the glass ceramic comprises 0 to 9.0,preferably 2.0 to 6.0 and particularly preferably 3.0 to 5.0 wt.-% P₂O₅.It is assumed that the P₂O₅ acts as nucleating agent.

It is also preferred that the glass ceramic comprises 1.0 to 8.0 and inparticular 2.0 to 7.0 wt.-% oxide of monovalent elements Me^(I) ₂Oselected from the group of K₂O, Na₂O, Rb₂O, Cs₂O and mixtures thereof.

The glass ceramic particularly preferably comprises at least one and inparticular all of the following oxides of monovalent elements Me^(I) ₂Oin the amounts specified:

Component wt.-% K₂O 0 to 5.0 Na₂O 0 to 2.0 Rb₂O 0 to 8.0 Cs₂O 0 to 7.0.

In a particularly preferred embodiment, the glass ceramic according tothe invention comprises 0 to 5.0, preferably 1.0 to 4.0 and particularlypreferably 2.0 to 3.5 wt.-% K₂O.

Furthermore, it is preferred that the glass ceramic comprises 1.0 to9.0, preferably 2.0 to 8.0 and particularly preferably 3.0 to 7.0 wt.-%oxide of divalent elements Me^(II)O selected from the group of CaO, MgO,SrO, ZnO and mixtures thereof.

In a further preferred embodiment, the glass ceramic comprises less than2.0 wt.-% BaO. The glass ceramic is in particular substantially freefrom BaO.

The glass ceramic preferably comprises at least one and in particularall of the following oxides of divalent elements Me^(II)O in the amountsspecified:

Component wt.-% CaO 0 to 3.0 MgO 0 to 6.0 SrO 0 to 4.0 ZnO 0 to 9.0

In a particularly preferred embodiment, the glass ceramic according tothe invention comprises 1.0 to 6.0, in particular 1.5 to 6.0, preferably2.0 to 5.5, particularly preferably 3.1 to 5.5 and quite particularlypreferably 3.4 to 5.0 wt.-% MgO.

A glass ceramic is further preferred which comprises 0 to 8.0,preferably 1.0 to 7.0 and particularly preferably 2.0 to 6.5 wt.-oxideof trivalent elements Me^(III) ₂O₃ selected from the group of Al₂O₃,B₂O₃, Y₂O₃, La₂O₃, Ga₂O₃, In₂O₃ and mixtures thereof.

The glass ceramic particularly preferably comprises at least one and inparticular all of the following oxides of trivalent elements Me^(III)₂O₃ in the amounts specified:

Component wt.-% Al₂O₃ 1.0 to 6.0   B₂O₃ 0 to 4.0 Y₂O₃ 0 to 5.0 La₂O₃ 0to 5.0 Ga₂O₃ 0 to 3.0 In₂O₃ 0 to 5.0

In a particularly preferred embodiment, the glass ceramic according tothe invention comprises 1.0 to 6.0 and preferably 2.0 to 5.0 wt.-%Al₂O₃.

Furthermore, a glass ceramic is preferred which comprises 0 to 10.0 andparticularly preferably 0 to 8.0 wt.-% oxide of tetravalent elementsMe^(IV)O₂ selected from the group of ZrO₂, TiO₂, SnO₂, CeO₂, GeO₂ andmixtures thereof.

The glass ceramic particularly preferably comprises at least one and inparticular all of the following oxides of tetravalent elements Me^(IV)O₂in the amounts specified:

Component wt.-% ZrO₂ 0 to 3.0 TiO₂ 0 to 4.0 SnO₂ 0 to 3.0 GeO₂ 0 to 9.0,in particular 0 to 8.0 CeO₂ 0 to 4.0.

In a further embodiment, the glass ceramic comprises 0 to 8.0,preferably 0 to 6.0 wt.-% oxide of pentavalent elements Me^(V) ₂O₅selected from the group of V₂O₅, Ta₂O₅, Nb₂O₅ and mixtures thereof.

The glass ceramic particularly preferably comprises at least one and inparticular all of the following oxides of pentavalent elements Me^(V)₂O₅ in the amounts specified:

Component wt.-% V₂O₅ 0 to 2.0 Ta₂O₅ 0 to 5.0 Nb₂O₅ 0 to 5.0

In a further embodiment, the glass ceramic comprises 0 to 5.0,preferably 0 to 4.0 wt.-% oxide of hexavalent elements Me^(VI)O₃selected from the group of WO₃, MoO₃ and mixtures thereof.

The glass ceramic particularly preferably comprises at least one and inparticular all of the following oxides Me^(VI)O₃ in the amountsspecified:

Component wt.-% WO₃ 0 to 3.0 MoO₃ 0 to 3.0

In a further embodiment, the glass ceramic according to the inventioncomprises 0 to 1.0 and in particular 0 to 0.5 wt.-% fluorine.

A glass ceramic is particularly preferred which comprises at least oneand preferably all of the following components in the amounts specified:

Component wt.-% SiO₂ 59.0 to 79.0 or 68.0 to 79.0 Li₂O 8.0 to 15.0  P₂O₅0 to 9.0 Me^(I) ₂O 1.0 to 8.0   Me^(II)O 1.0 to 9.0   Me^(III) ₂O₃ 0 to8.0 Me^(IV)O₂  0 to 10.0 Me^(V) ₂O₅ 0 to 8.0 Me^(VI)O₀₃ 0 to 5.0fluorine  0 to 1.0,

wherein Me^(I) ₂O, Me^(II)O, Me^(III) ₂O₃, Me^(IV)o₂, Me^(V) ₂O₅ andMe^(VI)O₃ have the above-specified meaning.

In a further particularly preferred embodiment, the glass ceramiccomprises at least one and preferably all of the following components inthe amounts specified:

Component wt.-% SiO₂ 59.0 to 79.0 or 68.0 to 79.0 Li₂O 8.0 to 15.0  P₂O₅0 to 9.0 K₂O 0 to 5.0 Na₂O 0 to 2.0 Rb₂O 0 to 8.0 Cs₂O 0 to 7.0 CaO 0 to3.0 MgO 0 to 6.0 SrO 0 to 4.0 ZnO 0 to 9.0 Al₂O₃ 1.0 to 6.0   B₂O₃ 0 to4.0 Y₂O₃ 0 to 5.0 La₂O₃ 0 to 5.0 Ga₂O₃ 0 to 3.0 In₂O₃ 0 to 5.0 ZrO₂ 0 to3.0 TiO₂ 0 to 4.0 SnO₂ 0 to 3.0 GeO₂ 0 to 9.0, in particular 0 to 8.0CeO₂ 0 to 4.0 V₂O₅ 0 to 2.0 Ta₂O₅ 0 to 5.0 Nb₂O₅ 0 to 5.0 WO₃ 0 to 3.0MoO₃ 0 to 3.0 fluorine  0 to 1.0.

Some of the above-named components can serve as colorants and/orfluorescent agents. The glass ceramic according to the invention canalso comprise still further colorants and/or fluorescent agents. Thesecan e.g. be selected from Bi₂O₃ or Bi₂O₅ and in particular from furtherinorganic pigments and/or oxides of d-block and f-block elements, suchas the oxides of Mn, Fe, Co, Pr, Nd, Tb, Er, Dy, Eu and Yb. With the aidof these colorants and fluorescent agents a simple dying of the glassceramic is possible in order to imitate the desired optical propertiesin particular of natural tooth material. It is surprising that this ispossible without problems despite the low quartz present as furthercrystal phase.

In a preferred embodiment of the glass ceramic the molar ratio of SiO₂to Li₂O lies in the range of from 2.2 to 4.1, preferably 2.2 to 3.8 andparticularly preferably 2.2 to 3.5. It is surprising that thepreparation of the glass ceramic according to the invention with lithiumsilicate as main crystal phase and low quartz as further crystal phaseis achieved within these broad ranges.

The term “main crystal phase” refers to the crystal phase which has thehighest proportion by mass of all the crystal phases present in theglass ceramic. The masses of the crystal phases are determined inparticular using the Rietveld method. A suitable process for thequantitative analysis of the crystal phases by means of the Rietveldmethod is described e.g. in M. Dittmer's doctoral thesis “Glasses andglass ceramics in the MgO—Al₂O₃—SiO₂ system with ZrO₂ as nucleatingagent”, University of Jena 2011.

It is preferred that the glass ceramic according to the inventioncomprises lithium disilicate or lithium metasilicate as main crystalphase. In a particularly preferred embodiment, the glass ceramicaccording to the invention comprises lithium disilicate as main crystalphase, as this glass ceramic has a particularly advantageous combinationof desirable properties.

In the case of a glass ceramic according to the invention with lithiummetasilicate as main crystal phase it is preferred that the glassceramic also comprises lithium disilicate as further crystal phase inaddition to low quartz.

It is preferred that the glass ceramic according to the invention has atleast 20 wt.-%, preferably 25 to 55 wt.-% and particularly preferably 30to 55 wt.-% lithium disilicate crystals.

It is further preferred that the glass ceramic according to theinvention has 0.2 to 28 wt.-% and particularly preferably 0.5 to 25wt.-% low quartz crystals.

The glass ceramic according to the invention can comprise, in additionto lithium silicate and low quartz, still further crystal phases, suchas apatite, caesium aluminosilicate and in particular lithium phosphate.However, the amount of cristobalite should be as small as possible, andin particular should be less than 1.0 wt.-%. It is particularlypreferred that the glass ceramic according to the invention issubstantially free from cristobalite.

The type and in particular the amount of the crystal phases formed canbe controlled by the composition of the starting glass as well as theheat treatment which is used to prepare the glass ceramic from thestarting glass. The examples illustrate this with reference to thevariation in the composition of the starting glass and the heattreatment used.

The glass ceramic has a high biaxial breaking strength of preferably atleast 200 MPa and particularly preferably 250 to 460 MPa. The biaxialbreaking strength was determined according to ISO 6872 (2008)(piston-on-three-ball test).

It is particularly surprising that, despite this high breaking strength,the glass ceramic according to the invention can be machined easily andquickly by means of computer-assisted milling and grinding apparatusesin order to give the glass ceramic e.g. the shape of a dentalrestoration.

The glass ceramic according to the invention has a coefficient ofthermal expansion CTE (measured in the range of 100 to 500° C.) ofpreferably 9.5 to 14.0·10⁻⁶K⁻¹. The CTE is determined according to ISO6872 (2008). The coefficient of thermal expansion is adjusted to adesired value in particular by the type and amount of the crystal phasespresent in the glass ceramic as well as the chemical composition of theglass ceramic.

The translucence of the glass ceramic was determined in the form of thecontrast value (CR value) according to British Standard BS 5612, andthis contrast value was preferably 40 to 92.

The particular combination of properties present in the case of theglass ceramic according to the invention even allows it to be used asdental material and in particular as material for the preparation ofdental restorations.

The invention likewise relates to various precursors with acorresponding composition from which the lithium silicate-low quartzglass ceramic according to the invention can be prepared by heattreatment. These precursors are a starting glass with a correspondingcomposition and a starting glass with nuclei with a correspondingcomposition. The term “corresponding composition” means that theseprecursors comprise the same components in the same amounts as the glassceramic, wherein the components with the exception of fluorine arecalculated as oxides, as is usual for glasses and glass ceramics.

The invention therefore also relates to a starting glass which comprisesthe components of the lithium disilicate-low quartz glass ceramicaccording to the invention.

The starting glass according to the invention therefore comprises inparticular suitable amounts of SiO₂ and Li₂O which are required to formthe glass ceramic according to the invention with lithium silicate asmain crystal phase and low quartz as further crystal phase. Further, thestarting glass can also comprise still other components, such as arespecified above for the lithium silicate-low quartz glass ceramicaccording to the invention. All those embodiments which are specified aspreferred for the components of the lithium silicate-low quartz glassceramic according to the invention are also preferred for the componentsof the starting glass.

The invention also relates to such a starting glass which comprisesnuclei for the crystallization of lithium metasilicate, lithiumdisilicate and/or low quartz.

The further precursor starting glass with nuclei can be produced firstby heat treatment of the starting glass. The lithium silicate-low quartzglass ceramic according to the invention can then be produced by heattreatment of this further precursor. It is preferred to form the lithiumsilicate-low quartz glass ceramic according to the invention by heattreatment of the starting glass with nuclei.

It is preferred to subject the starting glass to a heat treatment at atemperature of 400 to 600° C., in particular 450 to 550° C., for aperiod of preferably 5 to 120 min, in particular 10 to 60 min, in orderto produce the starting glass with nuclei for the crystallization oflithium metasilicate, lithium disilicate and/or low quartz.

It is further preferred to subject the starting glass with nuclei to aheat treatment at a temperature of 700 to 900° C. for a period of inparticular 1 to 120 min, preferably 5 to 120 min, particularlypreferably 10 to 60 min, in order to prepare the lithium silicate-lowquartz glass ceramic. To prepare the lithium silicate-low quartz glassceramic the heat treatment of the starting glass with nucleiparticularly preferably takes place at 700 to 880° C., in particular 750to 850° C., for a period of preferably 5 to 120 min, particularlypreferably 10 to 60 min.

The invention also relates to a process for the preparation of thelithium silicate-low quartz glass ceramic according to the invention, inwhich the starting glass or the starting glass with nuclei is subjectedto at least one heat treatment at a temperature of 700 to 900° C. for aperiod of in particular 1 to 120 min, preferably 5 to 120 min andparticularly preferably 10 to 60 min.

The starting glass and the starting glass with nuclei can be subjectedto the at least one heat treatment e.g. in the form of a solid glassblank, a powder compact or a powder.

The at least one heat treatment carried out in the process according tothe invention can also take place during a hot pressing or sintering-onof the starting glass according to the invention or of the startingglass with nuclei according to the invention.

In a preferred embodiment the process according to the inventioncomprises

-   (a) the heat treatment of the starting glass at a temperature of 400    to 600° C. in order to form the starting glass with nuclei, and-   (b) the heat treatment of the starting glass with nuclei at a    temperature of 700 to 900° C. in order to form the lithium    silicate-low quartz glass ceramic.

The duration of the heat treatments carried out in (a) and (b) is inparticular 5 to 120 min and preferably 10 to 60 min.

To prepare the starting glass, the procedure is in particular that amixture of suitable starting materials, such as carbonates, oxides,phosphates and fluorides, is melted at temperatures of in particular1300 to 1600° C. for 2 to 10 h. To achieve a particularly highhomogeneity, the obtained glass melt is poured into water in order toform a granular glass material, and the obtained granulate is thenmelted again.

The melt can then be poured into moulds in order to produce blanks ofthe starting glass, so-called solid glass blanks or monolithic blanks.

It is also possible to put the melt into water again in order to preparea granulate. This granulate can be pressed, after grinding andoptionally addition of further components, such as colorants andfluorescent agents, to form a blank, a so-called powder compact.

Finally, the starting glass can also be processed to form a powder aftergranulation.

The starting glass, e.g. in the form of a solid glass blank, a powdercompact or in the form of a powder, is then subjected to at least oneheat treatment. It is preferred that a first heat treatment is carriedout first in order to prepare a starting glass according to theinvention with nuclei which are suitable for forming lithiummetasilicate, lithium disilicate and/or low quartz crystals. The glasswith nuclei is then usually subjected to at least one furthertemperature treatment at a higher temperature in order to effectcrystallization of lithium silicate, in particular of lithiumdisilicate, and low quartz.

The glass ceramics according to the invention and the glasses accordingto the invention are present in particular in the form of powders,granulates or blanks of any shape and size, e.g. monolithic blanks, suchas platelets, cuboids or cylinders, or powder compacts, in unsintered,partially sintered or densely sintered form. They can easily be furtherprocessed in these forms. They can, however, also be present in the formof dental restorations, such as inlays, onlays, crowns, veneers, facetsor abutments.

Dental restorations, such as bridges, inlays, onlays, crowns, veneers,facets or abutments, can be prepared from the glass ceramics accordingto the invention and the glasses according to the invention. Theinvention therefore also relates to their use for the preparation ofdental restorations. It is preferred that the glass ceramic or the glassis given the shape of the desired dental restoration by pressing ormachining.

The pressing is usually carried out under increased pressure and atincreased temperature. It is preferred that the pressing is carried outat a temperature of 700 to 1200° C. It is further preferred to carry outthe pressing at a pressure of 2 to 10 bar. During pressing, the desiredchange in shape is achieved by viscous flow of the material used. Thestarting glass according to the invention and in particular the startingglass with nuclei according to the invention, and the lithiumsilicate-low quartz glass ceramic according to the invention, can beused for the pressing. The glasses and glass ceramics according to theinvention can be used in particular in the form of blanks in any shapeand size, e.g. solid blanks or powder compacts, e.g. in unsintered,partially sintered or densely sintered form.

The machining is usually carried out by material removal processes andin particular by milling and/or grinding. It is particularly preferredthat the machining is carried out during a CAD/CAM process. The startingglass according to the invention, the starting glass with nucleiaccording to the invention and the lithium silicate-low quartz glassceramic according to the invention can be used for the machining. Theglasses and glass ceramics according to the invention can be used inparticular in the form of blanks, e.g. solid blanks or powder compacts,e.g. in unsintered, partially sintered or densely sintered form. Thelithium silicate-low quartz glass ceramic according to the invention ispreferably used for the machining.

After the preparation of the dental restoration shaped as desired, e.g.by pressing or machining, it can still be heat-treated in order toreduce the porosity, e.g. of a porous powder compact used.

However, the glass ceramics according to the invention and the glassesaccording to the invention are also suitable as coating material fore.g. ceramics and glass ceramics. The invention is therefore alsodirected towards the use of the glasses according to the invention orthe glass ceramics according to the invention for coating in particularceramics and glass ceramics.

The invention also relates to a process for coating ceramics, metals,metal alloys and glass ceramics, in which glass ceramic according to theinvention or glass according to the invention is applied to the ceramicor glass ceramic and exposed to increased temperature.

This can be carried out in particular by sintering-on or joining of anoverstructure prepared by means of CAD/CAM using a suitable glass solderor adhesive, and preferably by pressing-on. In the case of sintering-on,the glass ceramic or the glass is applied to the material to be coated,such as ceramic or glass ceramic, in the usual way, e.g. as a powder,and then sintered at increased temperature. In the case of the preferredpressing-on, glass ceramic according to the invention or glass accordingto the invention is pressed on, e.g. in the form of powder compacts ormonolithic blanks, at an increased temperature of e.g. 700 to 1200° C.,and with the application of pressure, e.g. 2 to 10 bar. For this, inparticular the processes described in EP 231 773 and the press furnacedisclosed there can be used. A suitable furnace is e.g. the Programat EP5000 from Ivoclar Vivadent AG, Liechtenstein.

It is preferred that, after conclusion of the coating process, the glassceramic according to the invention is present with lithium silicate, inparticular lithium disilicate, as main crystal phase and low quartz asfurther crystal phase, as such a glass ceramic has particularly goodproperties.

Because of the above-described properties of the glass ceramicsaccording to the invention and the glasses according to the invention,these are suitable in particular for use in dentistry. A subject of theinvention is therefore also the use of the glass ceramics according tothe invention or the glasses according to the invention as dentalmaterial and in particular for the preparation of dental restorations oras coating material for dental restorations, such as crowns, bridges andabutments.

The invention is explained in more detail below with reference tonon-limiting examples.

EXAMPLES Examples 1 to 34—Composition and Crystal Phases

A total of 34 glasses and glass ceramics according to the invention withthe composition specified in Table I were prepared by meltingcorresponding starting glasses as well as subsequent heat treatments forcontrolled nucleation and crystallization.

The heat treatments used for controlled nucleation and controlledcrystallization are also specified in Table I. The following meaningsapply

T_(g) Glass transition temperature, determined by means of DSC T_(g) andt_(s) Temperature and time used for melting the starting glass T_(Kb)and t_(Kb) Temperature and time used for nucleation of the startingglass T_(c) and t_(c) Temperature and time used for the crystallizationT_(press) and t_(press) Temperature and time used for crystallization byhot pressing CR value Contrast value of the glass ceramic according toBritish Standard BS 5612 determined using: Apparatus: CM-3700dspectrometer (Konica- Minolta) Measurement parameters: Measurement area:7 mm × 5 mm Type of measurement: reflectance/ reflection Measurementrange: 400 nm-700 nm Sample size: Diameter: 15-20 mm Thickness: 2 mm +/−0.025 mm Plane parallelism: +/− 0.05 mm Surface roughness: about 18 μm.CTE Coefficient of thermal expansion of the glass ceramic according toISO 6872 (2008), measured in the range of 100 to 500° C. σ_(Biax)Biaxial breaking strength, measured according to dental standard ISO6872 (2008)

The amounts of the crystal phases were determined by means of theRietveld method. For this, powders of the respective glass ceramic wereused which were mixed with Al₂O₃ (product name: Taimicron TM-DAR, from:Taimei Chemicals, Co. Ltd., Japan) as internal standard in a ratio of 50wt.-% glass ceramic to 50 wt.-% Al₂O₃. This mixture was slurried withacetone in order to achieve as good a thorough mixing as possible. Themixture was then dried at about 80° C. Then a diffractogram in the range10 to 100° 2θ was acquired by means of a D8 Advance diffractometer fromBruker using Cu_(Kα) radiation and a step size of 0.014° 2θ. Thisdiffractogram was then evaluated with the TOPAS software from Bruker,and the phase proportions were determined. For all diffractograms alower limit of about 30 nm for the Li₃PO₄ crystallite size was used.

To produce the glasses and glass ceramics according to the invention thestarting glasses in a range of 100 to 200 g were first melted fromcustomary raw materials at 1500° C. or 1400° C. for a period of 1 to 3hours, wherein the melting was very easily possible without formation ofbubbles or streaks. By pouring the starting glasses into water, glassfrits were prepared which were then melted a second time at 1500° C. or1400° C. for 1 hour for homogenization.

A first heat treatment of the starting glasses at a temperature of 460to 550° C. led to the formation of glasses with nuclei. As a result of afurther heat treatment at 760 to 880° C., these nuclei-containingglasses crystallized to form glass ceramics with lithium silicate asmain crystal phase and low quartz as further crystal phase, as wasestablished by X-ray diffraction tests. Thus, lithium silicate-lowquartz glass ceramics according to the invention were obtained.

A) Solid Glass Blocks

In Examples 1-26, 28 and 31-34 the glass ceramics were prepared fromsolid glass blocks. For this, the obtained glass granulates were meltedagain at the temperature T_(S) for a period t_(S). The obtained melts ofthe starting glass were then poured into a graphite mould in order toproduce solid glass blocks. These glass monoliths were then stressrelieved at the temperature T_(Kb) for a period t_(Kb), wherebynucleation was able to take place. The nuclei-containing startingglasses were then heated to a temperature T_(C) for a period t_(C).Glass ceramics according to the invention with lithium disilicate asmain crystal phase and low quartz as additional phase were therebyformed, as could be established by X-ray diffraction tests at roomtemperature.

It is assumed that in this process variant a volume crystallization oflithium disilicate and low quartz has taken place.

B) Powder Compacts

In Example 27 the glass ceramic was prepared from powder compacts. Forthis, the obtained glass granulate was ground in a zirconium oxide millto a particle size of <90 μm. About 4 g of this powder was then pressedto form cylindrical blanks and sintered in a sinter furnace (Programat®from Ivoclar Vivadent AG) at a temperature T_(C) and a holding time oft_(C) to form dense glass ceramic bodies. A glass ceramic according tothe invention with lithium metasilicate as main crystal phase as well aslithium disilicate and low quartz as additional phases was formed by thesintering, as could be established by X-ray diffraction tests at roomtemperature.

C) Preparation of a Dental Restoration from Blocks According to A)

The glass ceramic blocks produced according to Examples 1-26, 28 and31-34 were machined in a CAD/CAM unit to form desired dentalrestorations, such as crowns. For this, the crystallized blocks wereprovided with a suitable holder, and then given the desired shape in aninLab MC XL grinding unit from Sirona Dental GmbH, Germany. For theprocessing of the blanks according to the invention it was possible touse the same grinding parameters as for commercial e.max CAD blocks,Ivoclar Vivadent, Liechtenstein.

D) Hot Pressing of the Glass Ceramic

In Example 19, for which T_(press) and t_(press) are specified, theglass ceramic was prepared from solid glass blocks by hot pressing.

For this, the obtained glass granulate was melted again at thetemperature T_(S) for a period t_(S). The obtained melt of the startingglass was then poured into a pre-heated steel mould in order to producerods. These monolithic glass rods were then stress relieved at atemperature T_(Kb) for a period t_(Kb), whereby nucleation was able totake place. The rods were then sawn to form small cylinders with a massof about 4 to 6 g. These small cylinders were then crystallized at atemperature T_(C) for a period of t_(C). The nucleated and crystallizedcylinders were then pressed to form a shaped body in a hot-pressingfurnace at the temperature T_(press) and for a holding time oft_(press). A glass ceramic according to the invention with lithiumdisilicate as main crystal phase and low quartz as further crystal phasehad formed after the hot-pressing, as could be established by X-raydiffraction tests of the formed shaped body at room temperature.

E) Sintering of a Nucleated Glass

In Example 29 the starting glass was melted at 1500° C. for 2 h and thenquenched in water. The obtained glass granulate was then nucleated at atemperature T_(Kb) and for a time t_(Kb). The nucleated starting glasswas comminuted to form a powder with an average particle size of 20 μm.A test piece was prepared from this nucleated glass powder to determinethe thermal expansion and to determine the optical properties, andcrystallized and densely sintered at a temperature of T_(C) and for atime t_(C). After the dense sintering a glass ceramic according to theinvention with lithium disilicate as main crystal phase and low quartzas further additional phase had formed, as could be established by X-raydiffraction tests of the formed shaped body at room temperature.

TABLE 1 Example No. 1 2 3 4 5 Composition wt.-% wt.-% wt.-% wt.-% wt.-%SiO₂ 74.3 73.3 72.0 72.0 74.9 Li₂O 11.2 12.6 13.3 12.3 10.7 K₂O 3.4 3.23.5 3.4 3.4 Rb₂O — — — — — MgO 4.4 1.4 4.5 4.4 4.4 CaO — 1.9 — — — SrO —— — — — Al₂O₃ 2.8 3.5 2.8 2.8 2.8 Ga₂O₃ — — — — — Er₂O₃ — — — 0.1 — CeO₂— — — 0.8 — V₂O₅ — — — 0.1 — P₂O₅ 3.9 4.1 3.9 3.9 3.8 F⁻ — — — — — Tb₄O₇— — — 0.3 — Tg/° C. 471 465 469 463 471 T_(s)/° C., t_(s)/min 1500, 1201520, 120 1500, 120 1500, 120 1500, 120 T_(Kb)/° C., t_(Kb)/min 500, 30480, 10 500, 30 500, 30 500, 30 T_(c)/° C., t_(c)/min 800, 30 800, 15800, 30 810, 20 800, 30 Main crystal phase Li₂Si₂O₅ (40.9) Li₂Si₂O₅Li₂Si₂O₅ (51.3) Li₂Si₂O₅ (43.4) Li₂Si₂O₅ (36.2) (wt.-%) Further crystalLow quartz Low quartz, Low quartz Low quartz Low quartz phases (17.5),Li₃PO₄ (0.2), (4.4), (20.7), (wt.-%) Li₃PO₄ (6.3) Li₃PO₄ (6.8) Li₃PO₄(6.0), Li₃PO₄ (5.4) σ_(Biax)/MPa 464 376 CR value 71.83 71.45 71.21 L*94.15 89.46 93.90 a* −0.45 0.48 −0.40 b* 3.44 13.22 3.92 CTE/10⁻⁶K⁻¹(100-500° C.) Example No. 6 7 8 9 10 Composition wt.-% wt.-% wt.-% wt.-%wt.-% SiO₂ 72.3 72.6 70.1 73.0 75.6 Li₂O 12.0 11.7 11.3 11.4 10.2 K₂O3.4 3.4 — 3.4 3.4 Rb₂O — — 6.5 — — MgO 4.4 4.4 4.2 4.4 4.3 CaO — — — — —SrO — — — — — Al₂O₃ 2.8 2.8 2.2 2.8 2.7 Ga₂O₃ — — — — — Er₂O₃ 0.1 0.10.1 0.1 — CeO₂ 0.8 0.8 0.7 0.6 — V₂O₅ 0.1 0.1 0.1 0.1 — P₂O₅ 3.9 3.8 4.53.8 3.8 F⁻ — — — — — Tb₄O₇ 0.3 0.3 0.3 0.4 — T_(g)/° C. 469 473 472 470480 T_(s)/° C., t_(s)/min 1500, 120 1500, 120 1500, 120 1500, 120 1500,120 T_(Kb)/° C., t_(Kb)/min 480, 60 520, 10 480, 120 470, 10 500, 30T_(c)/° C., t_(c)/min 800, 30 820, 10 800, 10 780, 30 800, 30 Maincrystal phase Li₂Si₂O₅ (42.7) Li₂Si₂O₅ (39.0) Li₂Si₂O₅ (30.0) Li₂Si₂O₅(38.4) Li₂Si₂O₅ (32.7) (wt.-%) Further crystal Low quartz Low quartz Lowquartz Low quartz Low quartz phases (10.2), (12.1), (7.1), (14.8),(24.2), (wt.-%) Li₃PO₄ (6.0) Li₃PO₄ (6.0) Li₃PO₄ (7.1) Li₃PO₄ (5.6)Li₃PO₄ (6.3) σ_(Biax)/MPa 371 395 456 326 347 CR value 69.27 68.94 77.1468.63 71.28 L* 89.78 89.68 90.06 90.29 94.07 a* 0.34 0.18 −0.13 0.85−0.46 b* 13.65 13.9 9.07 11.17 3.46 CTE/10⁻⁶K⁻¹ (100-500° C.) 10.8 11.311.5 Example No. 11 12 13 14 15 Composition wt.-% wt.-% wt.-% wt.-%wt.-% SiO₂ 72.9 72.2 70.2 72.4 70.4 Li₂O 11.3 11.6 12.5 10.9 12.1 K₂O2.1 3.4 3.3 3.4 3.1 Rb₂O — — — — — MgO 1.8 4.4 1.6 4.3 3.4 CaO 1.8 — 2.3— — SrO 3.3 — — — — Al₂O₃ 2.7 4.6 4.0 3.9 3.6 Ga₂O₃ — — — — 2.5 Er₂O₃ —— 0.2 0.2 0.1 CeO₂ — — 1.2 0.6 0.9 V₂O₅ — — 0.1 0.1 0.1 P₂O₅ 3.8 3.8 4.33.8 3.5 F⁻ 0.3 — — — — Tb₄O₇ — — 0.3 0.4 0.3 T_(g)/° C. 453 477 464 472462 T_(s)/° C., t_(s)/min 1500, 120 1500, 120 1500, 120 1500, 120 1500,120 T_(Kb)/° C., t_(Kb)/min 460, 90 500, 30 500, 10 480, 40 540, 10T_(c)/° C., t_(c)/min 800, 40 800, 30 800, 60 770, 60 790, 30 Maincrystal phase Li₂Si₂O₅ (45.0) Li₂Si₂O₅ (38.7) Li₂Si₂O₅ (38.1) Li₂Si₂O₅(34.4) Li₂Si₂O₅ (39.0) (wt.-%) Further crystal Low quartz Low quartz Lowquartz Low quartz Low quartz phases (19.3), (13.4), (9.4), (17.4),(9.9), (wt.-%) Li₃PO₄ (2.8), Li₃PO₄ (5.4) Li₃PO₄ (6.3) Li₃PO₄ (5.2)Li₃PO₄ (5.4) Ca₂Sr₃(PO₄)₃F (5.5) σ_(Biax)/MPa 397 350 377 285 CR value70.06 64.56 69.01 70.84 L* 89.22 85.82 90.67 86.98 a* 0.50 2.6 1.95 1.80b* 5.87 19.74 8.96 19.10 CTE/10⁻⁶K⁻¹ (100-500° C.) 10.6 10.8 Example No.16 17 18 19 20 Composition wt.-% wt.-% wt.-% wt.-% wt.-% SiO₂ 69.2 71.571.0 74.7 70.0 Li₂O 11.5 10.5 10.0 9.8 10.5 K₂O 3.2 3.3 3.3 3.3 3.2 Cs₂O— — — — — Rb₂O — — — — — MgO 3.1 3.5 3.8 4.3 3.8 CaO — — — — — SrO — — —— — ZnO — — — — — Al₂O₃ 3.1 2.8 3.0 2.9 3.8 Ga₂O₃ — — — — — La₂O₃ — —3.4 — — Y₂O₃ — 2.9 — — — In₂O₃ 4.7 — — — — Er₂O₃ 0.2 0.1 0.1 0.1 0.2ZrO₂ — — — — — SnO₂ — — — — — CeO₂ 1.0 0.6 1.2 0.8 0.5 MnO₂ — — — — —V₂O₅ 0.1 0.1 0.1 0.1 0.1 Ta₂O₅ — — — — 3.8 P₂O₅ 3.5 4.3 3.7 3.6 3.7 F⁻ —— — — — Tb₄O₇ 0.4 0.4 0.4 0.4 0.4 T_(g)/° C. 483 477 478 467 482 T_(s)/°C., t_(s)/min 1500, 120 1500, 120 1500, 120 1500, 120 1500, 120 T_(Kb)/°C., t_(Kb)/min 550, 30 480, 10 500, 40 470, 60 500, 20 T_(c)/° C.,t_(c)/min 770, 20 760, 10 760, 20 750, 30 760, 30 T_(press)/° C.,t_(press)/° C. 870, 25 Main crystal phase Li₂Si₂O₅ (32.4) Li₂Si₂O₅(27.0) Li₂Si₂O₅ (27.3) Li₂Si₂O₅ (28.8) Li₂Si₂O₅ (29.1) (wt.-%) Furthercrystal Low quartz Low quartz Low quartz Low quartz Low quartz phases(9.8), (19.9), (18.6), (24.3), (14.8), (wt.-%) Li₃PO₄ (4.9), Li₃PO₄(6.0) Li₃PO₄ (5.1) Li₃PO₄ (3.8) Li₃PO₄ (4.4) σ_(Biax)/MPa 299 290 320367 CR value 57.60 56.69 46.84 64.29 63.10 L* 85.77 90.49 84.38 90.689.91 a* 0.16 −0.50 0.05 0.38 1.70 b* 19.18 9.68 26.72 12.76 9.43CTE/10⁻⁶K⁻¹ (100-500° C.) 12.8 Example No. 21 22 23 24 25 Compositionwt.-% wt.-% wt.-% wt.-% wt.-% SiO₂ 72.9 68.8 69.5 73.2 73.7 Li₂O 12.511.4 11.5 11.7 11.5 K₂O 3.5 3.3 3.3 0.8 3.3 Cs₂O — — — 1.3 — Rb₂O — — —1.3 — MgO 4.4 3.2 1.1 2.9 — CaO — — 1.5 — — SrO — — 2.4 — 3.6 ZnO — —1.8 — — Al₂O₃ 2.8 3.2 2.7 2.7 2.5 Ga₂O₃ — — — — — La₂O₃ — — — — — Y₂O₃ —— — — — In₂O₃ — — — — — Er₂O₃ — 0.2 0.2 0.1 0.1 ZrO₂ — 2.1 — — — SnO₂ —2.6 — — — CeO₂ — 1.1 1.8 1.5 1.5 MnO₂ — — — 0.1 — V₂O₅ — 0.1 0.2 0.2 0.1Ta₂O₅ — — — — — P₂O₅ 3.9 3.6 3.7 3.8 3.3 F⁻¹ — — — — — Tb₄O₇ — 0.4 0.40.4 0.4 T_(g)/° C. 473 483 461 467 472 T_(s)/° C., t_(s)/min 1500, 1201500, 120 1500, 120 1500, 120 1500, 120 T_(Kb)/° C., t_(Kb)/min 500, 30490, 30 480, 30 500, 20 500, 70 T_(c)/° C., t_(c)/min 800, 30 770, 40800, 10 820, 30 830, 40 T_(press)/° C., t_(press)/° C. Main crystalphase Li₂Si₂O₅ (48.0) Li₂Si₂O₅ Li₂Si₂O₅ Li₂Si₂O₅ Li₂Si₂O₅ (37.3) (wt.-%)Further crystal Low quartz Low quartz Low quartz Low quartz Low quartzphases (6.5), Li₃PO₄ Li₃PO₄ Li₃PO₄ (14.7), (wt.-%) Li₃PO₄ (6.6), Li₃PO₄(25.1) σ_(Biax)/MPa 487 CR value 74.98 53.15 L* 94.16 79.74 a* −0.623.58 b* 3.40 34.15 CTE/10⁻⁶K⁻¹ (100-500° C.) Example No. 26 27 28 29Composition wt.-% wt.-% wt.-% wt.-% SiO₂ 73.0 74.8 68.9 75.8 Li₂O 11.713.3 12.2 10.5 K₂O 3.4 3.6 3.3 3.4 Cs₂O — — — — Rb₂O — — — — MgO 4.4 1.71.4 3.6 CaO — 2.4 2.1 — SrO — — — — ZnO — — — — Al₂O₃ 3.7 4.2 3.9 2.9Ga₂O₃ — — — — La₂O₃ — — — — Y₂O₃ — — — — In₂O₃ — — — — Er₂O₃ — — — —ZrO₂ — — — — SnO₂ — — — — CeO₂ — — — — MnO₂ — — — — V₂O₅ — — — — Ta₂O₅ —— — — P₂O₅ 3.8 — 8.2 3.8 F⁻ — — — — Tb₄O₇ — — — — T_(g)/° C. 457 471 469T_(s)/° C., t_(s)/min 1500, 120 1500, 180 1500, 150 1500, 120 T_(Kb)/°C., t_(Kb)/min 500, 30 — 490, 10 500, 30 T_(c)/° C., t_(c)/min 800, 30780, 10 800, 30 880, 1 T_(press)/° C., t_(press)/° C. Main crystal phaseLi₂Si₂O₅ (45.0) Li₂SiO₃, Li₂Si₂O₅, Li₂Si₂O₅, (wt.-%) Further crystal Lowquartz Low quartz Low quartz Low quartz phases (12.8), Li₂Si₂O₅, Li₃PO₄Li₃PO₄ (wt.-%) Li₃PO₄ (6.0), Li₃PO₄ σ_(Biax)/MPa 320 CR value 67.66 76.6L* 91.17 94 a* 0.08 −0.21 b* 4.69 2.55 CTE/10⁻⁶K⁻¹ (100-500° C.) 12.3Example No. 30 31 32 33 34 Composition wt.-% wt.-% wt.-% wt.-% wt.-%SiO₂ 64.4 67.1 69.8 71.6 59.7 Li₂O 14.6 13.3 11.9 11.1 12.9 Na₂O — — 1.61.9 — K₂O 3.3 3.3 — — 3.2 Cs₂O — — 5.0 3.7 — Rb₂O — — — — — MgO — — 3.93.2 0.2 CaO — — — — — SrO — — — — — ZnO 8.7 8.6 — — 8.3 Al₂O₃ 2.7 2.72.7 2.7 2.6 Ga₂O₃ — — — — — La₂O₃ — — — — — Er₂O₃ — — 0.1 0.1 — ZrO₂ — —— — — SnO₂ — — — — — CeO₂ — — 0.8 1.5 — GeO₂ — — — — 8.9 MnO₂ — — — — —V₂O₅ — — 0.1 0.1 — Ta₂O₅ — — — — — P₂O₅ 6.3 5.0 3.8 3.7 4.2 F⁻ — — — — —Tb₄O₇ — — 0.3 0.4 — T_(g)/° C. 455 459 458 463 T_(s)/° C., t_(s)/min1500, 1500, 1500, 120 1500, 120 1400, 120 120 120 T_(Kb)/° C.,t_(Kb)/min 500, 30 500, 30 500, 30 500, 30 500, 30 T_(c)/° C., t_(c)/min840, 30 850, 30 800, 30 800, 30 820, 30 T_(press)/° C., t_(press)/° C.Main crystal phase Li₂Si₂O₅ , Li₂Si₂O₅, Li₂Si₂O₅, Li₂Si₂O₅ (33.8)Li₂Si₂O₅ , (wt.-%) Further crystal Low Low Low quartz, Li₃PO₄, Lowquartz, (15.6) Low quartz, phases quartz, quartz, Cs_(0.809)AlSi₅O₁₂Li₃PO₄, (5.8) Li₃PO₄ (wt.-%) Li₃PO₄ Li₃PO₄ Cs_(0.809)AlSi₅O₁₂ (10.0)σ_(Biax)/MPa 458 485 516 368 CR value 90.90 86.57 73.4 73.54 L* 95.8795.52 90.36 82.05 a* −0.24 −0.24 0.32 4.63 b* 0.84 0.66 11.49 26.02CTE/10⁻⁶K⁻¹ (100-500° C.)

1. Lithium silicate-low quartz glass ceramic, which comprises lithiumsilicate as main crystal phase and low quartz as further crystal phase.2. Glass ceramic according to claim 1, which comprises 59.0 to 79.0. 3.Glass ceramic according to claim 1, which comprises 8.0 to 15.0 wt.-%Li₂O.
 4. Glass ceramic according to claim 1, which comprises 0 to 9.0wt.-% P₂O₅.
 5. Glass ceramic according to claim 1, which comprises 1.0to 8.0 wt.-% oxide of monovalent elements Me^(I) ₂O selected from thegroup of K₂O, Na₂O, Rb₂O, Cs₂O and mixtures thereof.
 6. Glass ceramicaccording to claim 1, which comprises 0 to 5.0 wt.-% K₂O.
 7. Glassceramic according to claim 1, which comprises 1.0 to 9.0 wt.-% oxide ofdivalent elements Me^(II)O selected from the group of CaO, MgO, SrO, ZnOand mixtures thereof.
 8. Glass ceramic according to claim 1, whichcomprises 1.0 to 6.0 wt.-% MgO.
 9. Glass ceramic according to claim 1,which comprises 0 to 8.0 wt.-% oxide of trivalent elements Me^(III) ₂O₃selected from the group of Al₂O₃, B₂O₃, Y₂O₃, La₂O₃, Ga₂O₃, In₂O₃ andmixtures thereof.
 10. Glass ceramic according to claim 1, whichcomprises 1.0 to 6.0 wt.-% Al₂O₃.
 11. Glass ceramic according to claim1, which comprises SiO₂ and Li₂O in a molar ratio in the range of from2.2 to 4.1.
 12. Glass ceramic according to claim 1, which compriseslithium disilicate or lithium metasilicate as main crystal phase. 13.Glass ceramic according to claim 1, which has at least 20 wt.-% lithiumdisilicate crystals.
 14. Glass ceramic according to claim 1, which has0.2 to 28 wt.-% low quartz crystals.
 15. Starting glass, which comprisesthe components of the glass ceramic according to claim
 1. 16. Startingglass according to claim 15, which comprises nuclei for thecrystallization of lithium metasilicate, lithium disilicate and/or lowquartz.
 17. Glass ceramic comprising lithium silicate as main crystalphase and low quartz as further crystal phase or starting glasscomprising nuclei for the crystallization of lithium metasilicate,lithium disilicate and/or low quartz, wherein the glass ceramic and thestarting glass are present in the form of a powder, a granulate, a blankor a dental restoration.
 18. Process for the preparation of the glassceramic according to claim 1, in which a starting glass comprisingnuclei for the crystallization of lithium metasilicate, lithiumdisilicate and/or low quartz is subjected to at least one heat treatmentin the range of 700° to 900° C.
 19. Process according to claim 18, inwhich (a) the starting glass is subjected to a heat treatment at atemperature of 400 to 600° C. in order to form the starting glass withnuclei, and (b) the starting glass with nuclei is subjected to a heattreatment at a temperature of 700 to 900° C. in order to form thelithium silicate-low quartz glass ceramic.
 20. Process of using theglass ceramic according to claim 1 as dental material, for coatingdental restorations or for the preparation of dental restorations. 21.Process according to claim 20, wherein the glass ceramic is given ashape of the desired dental restoration comprising a bridge, inlay,onlay, veneer, abutment, partial crown, crown or facet, and ismanufactured by pressing or machining.
 22. Process for the preparationof a dental restoration comprising a bridge, inlay, onlay, veneer,abutment, partial crown, crown or facet, in which the glass ceramicaccording to claim 1 is given the shape of the desired dentalrestoration by pressing or machining.